CN111286676A - Production method of high crack-arresting marine steel plate - Google Patents
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Abstract
The production method of the marine steel plate with high crack resistance comprises the following steps of forming the chemical components by weight percent, wherein the chemical components comprise, by weight, 0.05-0.08% of C, 0.10-0.50% of Si, 1.40-1.80% of Mn, not more than 0.012% of P, not more than 0.003% of S, 0.02-0.05% of Nb, 0.008-0.02% of Ti, 0.015-0.05% of Al, 0.20-0.50% of Ni, not more than 0.35% of Cu, and not more than 0.25% of Gr; the key process steps comprise smelting, continuous casting, heating, rolling and cooling, a low-carbon high-manganese Nb-Ti-Ni multi-microalloying component design system is adopted, LF + VD composite refining and ultra-fast cooling technologies are combined, the high-strength ship plate with the yield strength of 460-550 MPa and the tensile strength of 570-720 MPa is produced, the maximum thickness can reach 80mm, the high-strength steel plate with high strength and toughness, weldability and crack resistance is obtained, and the use requirement of the crack-resistant steel plate at the key position of the ultra-large container ship can be well met.
Description
Technical Field
The invention belongs to the technical field of metallurgy, and relates to a production method of a high-strength marine steel plate with excellent crack arrest performance.
Background
With the development of economy and the increase of trade volume, container ships gradually develop in a large scale, the load bearing capacity of the upper structure of the deck of the container ship is larger and larger, and some key parts of the container ships, such as a main deck, a roof strake, a hatch coaming and the like, cannot meet the use requirements of a common high-strength ship plate due to the requirements of high strength, high toughness and high crack arrest performance. For example, 18000TEU ultra-large container ship, the thickness of the hatch coaming plate reaches 80mm, and the steel amount of the crack arrest steel EH47 is about 2000 tons/ship. The crack arrest steel plate has been developed in japan as early as 90 s in the 20 th century, and in 2008, japan steel and mitsubishi are combined to be worked, and a new type of high tensile strength steel, "HTS 47", was successfully developed and used for the first time in japan shipyards. In 2013, the international ship association (IACS) and some classification societies refer to the development experience of japan, a 47 kg-class steel plate standard for container ships is specially established for key parts of a large container ship plate, and the brittle fracture tests such as the ESSO test and the double tensile test are listed as methods for testing the crack arrest performance of the steel plate.
Chinese patent CN 101341269 a, "high strength thick steel plate with excellent crack arrest performance", mainly controls the difference of the structure, grain boundary density and texture of the steel plate in the thickness direction, so that the difference of the crack propagation direction occurs at different thickness positions of the steel plate during cracking, thereby increasing the crack arrest performance of the steel plate by increasing the crack propagation resistance. However, the cooling ability of the thick plate produced therefrom is substantially insufficient, and the brittle structure at the 1/2 th position of the plate thickness affects the crack-stopping property of the steel plate. This method has little improvement in crack arrest and does not fundamentally improve the ductile structure at the 1/2 site. Chinese patent CN 102994874A, "high-grade crack-arresting toughness steel plate with 500Mpa yield strength and production method thereof", discloses a method for refining grains and preventing crack from expanding by a method of rough rolling, then rapidly cooling to the vicinity of Ar3 transformation point and finish rolling. However, the method adopts low-temperature impact toughness and NDT ductile-brittle transition temperature to measure the crack-arresting performance of the steel plate, has no scientificity and rigidness, only can indicate that the toughness of the steel plate is good, and cannot prove that the crack-arresting performance of the steel plate is excellent, but only an ESSO test or a double tensile test is an internationally-accepted standard test for measuring the crack-arresting performance of the steel plate.
Disclosure of Invention
The invention aims to provide a production method of a high crack arrest marine steel plate, which represents that the maximum thickness of EH47 of a steel type reaches 80mm, the yield strength is 460-550 MPa, the tensile strength is 570-720 MPa, the core impact toughness at low temperature of minus 40 ℃ reaches more than 200J, the non-plastic transition temperature is below minus 60 ℃, and the crack arrest coefficient Kca at minus 10 ℃ is more than or equal to 6000N/mm through the test of a gradient temperature type double tensile test3/2And the use requirements of the crack arrest steel plates at the key parts of the ultra-large container ship can be well met.
The technical scheme of the invention is as follows:
a production method of a high crack-arresting marine steel plate comprises the following chemical components in percentage by weight: c =0.05% -0.08%, Si =0.10% -0.50%, Mn =1.40% -1.80%, P is less than or equal to 0.012%, S is less than or equal to 0.003%, Nb =0.02% -0.05%, Ti =0.008% -0.02%, Al =0.015% -0.05%, Ni =0.20% -0.50%, Cu is less than or equal to 0.35%, Gr is less than or equal to 0.25%, and the balance is Fe and inevitable impurities; the key process steps comprise:
smelting: the steel tapping of the converter is less than or equal to 0.008 percent for [ P ] and less than or equal to 0.05 percent for [ C ], an LF + VD refining process is adopted, argon is blown in the whole refining process of an LF furnace, slagging and deoxidation are carried out, and the white slag holding time is more than or equal to 20 min; VD vacuum degassing treatment, wherein the vacuum is kept for 18-25 min under the condition that the vacuum degree is less than 0.5tor, the [ N ] of the discharged molten steel is less than or equal to 40ppm, the [ H ] is less than or equal to 1.5ppm, and the [ O ] is less than or equal to 20 ppm;
continuous casting: the whole-process protective casting is adopted, and the thickness of a casting blank is 300 mm;
heating: the heating temperature of the casting blank is 1150-1180 ℃, and the soaking time is more than or equal to 30 min;
rolling: two-stage rolling is adopted, the finish rolling temperature of the first stage is more than or equal to 980 ℃, the thickness of the intermediate blank is more than or equal to 2 times of the thickness of a finished product, and the finish rolling temperature of the second stage is controlled to be 760-800 ℃;
and (3) cooling: and (3) directly feeding the rolled steel plate into water for forced cooling, wherein the cooling rate of the core part of the steel plate is 6-15 ℃/S until the final cooling temperature is 200-400 ℃, and the temperature of red returning is controlled at 400-460 ℃.
The thickness of the high crack-arresting marine steel plate produced by the method is 40-80 mm, and the microstructure is a microstructure which takes fine acicular ferrite as a matrix and is dispersed with a small amount of degenerated pearlite.
The invention principle is as follows:
the chemical composition design is mainly considered for crack resistance and weldability, and the steel should have low carbon equivalent and Pcm value while requiring high strength and good low-temperature toughness. The low-carbon high-manganese component design is adopted, the improvement of the C content can improve the strength and reduce the Ar3 temperature, but the low-temperature toughness, the crack arrest performance and the welding performance of the steel are deteriorated, so the final C content is controlled to be less than or equal to 0.08 percent by means of converter tapping (C) being less than or equal to 0.005 percent and the like, and when the C content is less than 0.05 percent, the strength of the steel plate is influenced; manganese is a weak carbide-forming element which can lower the austenite transformation temperature, refine ferrite grains, and contribute to the improvement of the strength and toughness of the steel sheet, and therefore, the lower limit of manganese design is 1.40% in the composition design, but when the content exceeds 1.80%, the central segregation is aggravated, causing severe deterioration of the crack arrest property.
In order to ensure crack arrest and weld HAZ toughness, the molten steel must have a high degree of purity. P, S is a harmful impurity element, the phosphorus content at the end point is less than or equal to 0.012 percent and the sulfur content is less than or equal to 0.003 percent by controlling [ P ] in the tapping of the converter to be less than or equal to 0.008 percent, by controlling the LF + VD composite refining process, the white slag holding time to be more than or equal to 20min, the VD furnace vacuum-maintaining time to be 18-25 min and the like, and the contents of other impurities and harmful gases in the molten steel are reduced.
In order to improve the crack arrest performance without influencing the welding performance, alloy elements such as Nb, Ti, Ni and the like are added in a compounding way on the basis of C-Mn steel solid solution strengthening, and the effects of grain refinement, precipitation strengthening, phase change strengthening and the like are fully exerted to achieve the purposes of high strength and toughness, high crack arrest performance and excellent welding performance.
Nb is used as an important microalloy element, more than 0.02 percent of Nb is added, fine carbide and nitride can be formed, the growth of austenite grains is inhibited, and the primary austenite is promoted to be recrystallized by combining the first-stage finish rolling temperature of more than or equal to 980 ℃; the final rolling temperature of the second stage is controlled to be 760-800 ℃, the recrystallization of austenite is inhibited, the deformation effect is maintained, and therefore grains are refined and phase change particles are provided. However, when the Nb content is more than 0.05%, niobium carbonitride and the like precipitate in large amounts in the steel sheet and grow, significantly affecting the crack arrest properties of the steel sheet and causing coarsening of crystal grains in the heat affected zone during welding.
Micro Ti treatment is carried out on the steel, and the addition of Ti with the content of more than 0.008 is beneficial to forming TiN pinning crystal boundary when the heating temperature is 1150-1180 ℃, inhibiting excessive growth of austenite grains, refining the grains in the rolling process and improving the crack arrest performance and the welding performance of the steel plate; however, if the Ti content is more than 0.02%, some Ti composite inclusions are formed, which become a fracture origin in the steel and are very harmful to the crack arrest performance of the steel.
Ni is also particularly key to improving the crack arrest performance of the steel plate, and can effectively improve the hardenability of the steel plate and improve the low-temperature toughness. When the content is more than 0.2%, an ultra-fast cooling process is combined, the cooling rate after rolling is controlled to be 6-15 ℃/S, the temperature of red return is controlled to be 400-460 ℃, a tissue taking fine acicular ferrite as a matrix is formed, the expansion of cracks can be effectively inhibited, and the crack arrest performance is improved; however, since Ni is expensive and the addition of too much Ni increases the production cost, the upper limit is set to 0.5%.
In order to ensure that the yield strength of the steel plate is more than or equal to 460Mpa and improve the hardenability of the thick steel plate, more than one element of Cu less than or equal to 0.35 percent and Gr less than or equal to 0.25 percent can be selectively added into the steel plate, but when the addition amount is excessive, the crack resistance and the welding performance of the steel plate can be reduced, and the manufacturing cost is increased.
The invention mainly improves the hardenability of the steel plate in the aspect of component design, improves the cooling rate of the thick steel plate and reduces the final cooling temperature by an ultra-fast cooling technology, and finally obviously improves the crack arrest toughness of the steel plate by increasing the content of fine acicular ferrite of a toughness structure in the thickness direction, particularly in the 1/2 position of the steel plate.
The invention has the beneficial effects that:
a. the invention adopts a low-carbon high-manganese Nb-Ti-Ni multi-element microalloying component design system and an LF + VD composite refining technology, strictly controls P, S content and the purity of molten steel, and adopts a series of new rolling technologies such as high temperature and high pressure, TMCP controlled rolling, ultra-fast cooling and the like to successfully develop the ultra-thick steel plate with high strength and toughness and high crack arrest performance of fine acicular ferrite and a small amount of degenerated pearlite tissues, thereby laying the foundation for the production of the cracked steel plate.
b. The method breaks through the TMCP process limit, replaces the traditional heat treatment process, gives full play to the equipment advantages, adopts 300 continuous casting billets to produce the ultra-thick steel plate with the yield strength of more than 460Mpa, has the maximum thickness of 80mm, reduces the alloy content and the production cost while ensuring the product quality, and promotes the research and development process of new varieties of economical, low-carbon and environment-friendly steel.
c. The present invention utilizes the existing equipment and technological conditions of steel plant, and has high production efficiency, low power consumption and no increase in investment and production cost.
d. The product produced by the method can be widely applied to the fields of shipbuilding, bridges, pressure vessels, buildings, engineering machinery and the like, and the crack arrest capability of the steel plate is ensured.
Drawings
FIG. 1 is a microstructure of a core portion of a steel sheet according to example 1 of the present invention.
FIG. 2 is a graph showing the relationship between the crack arrest toughness and the crack arrest temperature of the steel sheet of example 1 of the present invention.
Detailed Description
The invention will be further illustrated with reference to the following examples:
example 1:
a production method of a high crack arrest ship steel plate produces an EH47 steel plate with the thickness of 80mm, wherein the steel comprises the following chemical components by weight percentage of C =0.06%, Si =0.21%, Mn = 1.62%, P =0.009%, S =0.0017%, Nb =0.039%, Ti =0.015%, Al =0.044%, Ni =0.48%, Cu =0.28%, Gr =0.18%, and the balance of Fe and inevitable impurities. The key process steps comprise:
smelting: tapping by a converter, wherein P =0.006% and C =0.028%, an LF + VD refining process is adopted, argon is blown in the whole refining process of the LF furnace, slagging and deoxidation are carried out, white slag is kept for 21min, VD vacuum degassing treatment is carried out, the vacuum is kept for 23min under the condition that the vacuum degree is below 0.5tor, the outbound molten steel is N =38ppm, H =1.5ppm and O =16 ppm;
continuous casting: the whole-process protective casting is adopted, and the thickness of a casting blank is 300 mm;
heating: the heating temperature of the casting blank is 1175 ℃, and the soaking time is 35 min;
rolling: the finish rolling temperature of the first stage is 1023 ℃, the intermediate billet is 160mm, and the finish rolling temperature of the second stage is 785 ℃;
and (3) cooling: and (3) directly cooling the rolled steel plate in water, and forcibly cooling the steel plate by adopting a DQ high-pressure water pump of Mulpic, wherein the cooling rate of the core part of the steel plate is 6 ℃/S, the final cooling temperature is 215 ℃, and the temperature of red returning is 405 ℃.
The mechanical properties of the steel sheet are shown in Table 1.
Example 2:
a production method of a high crack arrest ship steel plate produces 60mm EH47 steel plate, wherein the steel comprises the following chemical components by weight percent of C =0.07%, Si =0.18%, Mn = 1.60%, P =0.011%, S =0.0025%, Nb =0.035%, Ti =0.018%, Al =0.039%, Ni =0.42%, Cu =0.25%, Gr =0.16%, and the balance of Fe and inevitable impurities. The key process steps comprise:
smelting: tapping steel from the converter, wherein P =0.008% and C =0.041%, adopting an LF + VD refining process, blowing argon in the whole refining process of the LF furnace, slagging and deoxidizing, and keeping white slag for 22 min; VD vacuum degassing treatment, wherein the vacuum degree is below 0.5tor, the vacuum maintaining time is 22min, the outlet molten steel is N =40ppm, H =1.5ppm and O =18 ppm;
continuous casting: the whole-process protective casting is adopted, and the thickness of a casting blank is 300 mm;
heating: heating the casting blank at 1162 ℃ for 30 min;
rolling: two-stage rolling is adopted, wherein the finish rolling temperature of the first stage is 1048 ℃, the intermediate billet is 140mm, and the finish rolling temperature of the second stage is 783 ℃;
and (3) cooling: and (3) directly cooling the rolled steel plate in water, and forcibly cooling the steel plate by adopting a DQ high-pressure water pump of Mulpic, wherein the cooling rate of the core part of the steel plate is 8 ℃/S, the final cooling temperature is 328 ℃, and the temperature of red return is 445 ℃.
The mechanical properties of the steel sheet are shown in Table 1.
Example 3:
a production method of a high crack-arrest marine steel plate is used for producing a 40mm EH47 steel plate, and the steel comprises the following chemical components in percentage by weight: c =0.05%, Si =0.22%, Mn = 1.52%, P =0.008%, S =0.0023%, Nb =0.035%, Ti =0.015%, Al =0.045%, Ni =0.25%, Cu =0.15%, Gr =0.15%, and the balance Fe and unavoidable impurities. The key process steps comprise:
smelting: tapping by a converter, wherein P =0.008% and C =0.032%, adopting an LF + VD refining process, blowing argon in the whole refining process of an LF furnace, slagging and deoxidizing, and keeping white slag for 21 min; VD vacuum degassing treatment, wherein the vacuum degree is below 0.5tor, the vacuum maintaining time is 20min, the outlet molten steel is N =35ppm, H =1.5ppm and O =18 ppm;
continuous casting: the whole-process protective casting is adopted, and the thickness of a casting blank is 300 mm;
heating: the heating temperature of the casting blank is 1155 ℃, and the soaking time is 30 min;
rolling: two-stage rolling is adopted, the finish rolling temperature of the first stage is 1053 ℃, the intermediate billet is 120mm, and the finish rolling temperature of the second stage is controlled at 798 ℃;
and (3) cooling: directly cooling the rolled steel plate in water by adopting forced cooling, wherein the cooling rate of the core part of the steel plate is 15 ℃/S, the final cooling temperature is 384 ℃, and the re-reddening temperature is 458 ℃.
The mechanical properties of the steel sheet are shown in Table 1.
TABLE 1 mechanical Properties of the steels in the examples
As can be seen from the test results in Table 1, the steel plate produced by the method of the present invention still has yield strength of 460MPa when the thickness reaches 80mmIn addition, the impact toughness performance of the core part at the temperature of minus 40 ℃ can reach more than 200J. The NDTT test result of the steel plate adopting the P-2 pattern shows that the non-plastic transition temperature of the steel plate is below minus 60 ℃, and the steel plate has lower non-plastic transition temperature. The crack arrestability of the steel sheet of example 1 was examined by a gradient temperature type double tensile crack arrestability test, as shown in FIG. 2, the Kca value of crack arrestability at-10 ℃ was 6000N/mm3/2The steel plate has high crack arrest performance, and can well meet the use requirements of key parts of the ultra-large container ship.
Claims (1)
1. A production method of a high crack arrest ship steel plate is characterized in that: the steel comprises, by weight, 0.05-0.08% of C, 0.10-0.50% of Si, 1.40-1.80% of Mn, less than or equal to 0.012% of P, less than or equal to 0.003% of S, 0.02-0.05% of Nb, 0.008-0.02% of Ti, 0.015-0.05% of Al, 0.20-0.50% of Ni, less than or equal to 0.35% of Cu, less than or equal to 0.25% of Gr, and the balance of Fe and inevitable impurities; the key process steps comprise:
smelting: the steel tapping of the converter is less than or equal to 0.008 percent for [ P ] and less than or equal to 0.05 percent for [ C ], an LF + VD refining process is adopted, argon is blown in the whole refining process of an LF furnace, slagging and deoxidation are carried out, and the white slag holding time is more than or equal to 20 min; VD vacuum degassing treatment, wherein the vacuum is kept for 18-25 min under the condition that the vacuum degree is less than 0.5tor, the [ N ] of the discharged molten steel is less than or equal to 40ppm, the [ H ] is less than or equal to 1.5ppm, and the [ O ] is less than or equal to 20 ppm;
continuous casting: adopting whole-process protective casting;
heating: the heating temperature of the casting blank is 1150-1180 ℃, and the soaking time is more than or equal to 30 min;
rolling: two-stage rolling is adopted, the finish rolling temperature of the first stage is more than or equal to 980 ℃, the thickness of the intermediate blank is more than or equal to 2 times of the thickness of a finished product, and the finish rolling temperature of the second stage is controlled to be 760-800 ℃;
and (3) cooling: directly feeding the rolled steel plate into water for forced cooling, wherein the cooling rate of the center of the steel plate is 6-15 ℃/S until the final cooling temperature is 200-400 ℃, and the temperature of red returning is controlled at 400-460 ℃;
the high crack-arresting marine steel plate is 40-80 mm thick, and the microstructure is a microstructure with fine acicular ferrite as a matrix and a small amount of degenerated pearlite dispersedly distributed.
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| CN112501504A (en) * | 2020-11-13 | 2021-03-16 | 南京钢铁股份有限公司 | BCA 2-grade container ship crack arrest steel plate and manufacturing method thereof |
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| CN115807192A (en) * | 2022-12-12 | 2023-03-17 | 湖南华菱湘潭钢铁有限公司 | Low-carbon 420 MPa-level TMCP structural steel and production method thereof |
| CN115976424A (en) * | 2022-12-14 | 2023-04-18 | 南阳汉冶特钢有限公司 | DH40 crack arrest steel plate for ocean platform and production method thereof |
Citations (6)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| CN104789898A (en) * | 2015-05-07 | 2015-07-22 | 湖南华菱湘潭钢铁有限公司 | Production method of ultrahigh-strength anti-cracking thick steel plate |
| CN107502821A (en) * | 2017-08-29 | 2017-12-22 | 江阴兴澄特种钢铁有限公司 | The economical X 70 pipeline steel plate and its manufacture method used under a kind of special think gauge ultra-low temperature surroundings |
| CN109182919A (en) * | 2018-11-22 | 2019-01-11 | 湖南华菱湘潭钢铁有限公司 | A kind of production method of heterogeneous structure high-toughness ship plate steel EH47 |
| CN109182702A (en) * | 2018-11-22 | 2019-01-11 | 湖南华菱湘潭钢铁有限公司 | A kind of production method of heterogeneous structure high-toughness ship plate steel EH40 |
| CN109576585A (en) * | 2018-12-25 | 2019-04-05 | 江阴兴澄特种钢铁有限公司 | A kind of van container EH47 crack arrest steel peculiar to vessel and its manufacturing method |
| CN109972033A (en) * | 2019-03-17 | 2019-07-05 | 湖南华菱湘潭钢铁有限公司 | A kind of production method of the super-thick steel plate Q460E of low-carbon-equivalent |
-
2020
- 2020-03-31 CN CN202010246601.6A patent/CN111286676A/en active Pending
Patent Citations (6)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| CN104789898A (en) * | 2015-05-07 | 2015-07-22 | 湖南华菱湘潭钢铁有限公司 | Production method of ultrahigh-strength anti-cracking thick steel plate |
| CN107502821A (en) * | 2017-08-29 | 2017-12-22 | 江阴兴澄特种钢铁有限公司 | The economical X 70 pipeline steel plate and its manufacture method used under a kind of special think gauge ultra-low temperature surroundings |
| CN109182919A (en) * | 2018-11-22 | 2019-01-11 | 湖南华菱湘潭钢铁有限公司 | A kind of production method of heterogeneous structure high-toughness ship plate steel EH47 |
| CN109182702A (en) * | 2018-11-22 | 2019-01-11 | 湖南华菱湘潭钢铁有限公司 | A kind of production method of heterogeneous structure high-toughness ship plate steel EH40 |
| CN109576585A (en) * | 2018-12-25 | 2019-04-05 | 江阴兴澄特种钢铁有限公司 | A kind of van container EH47 crack arrest steel peculiar to vessel and its manufacturing method |
| CN109972033A (en) * | 2019-03-17 | 2019-07-05 | 湖南华菱湘潭钢铁有限公司 | A kind of production method of the super-thick steel plate Q460E of low-carbon-equivalent |
Cited By (10)
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|---|---|---|---|---|
| CN108914008A (en) * | 2018-08-10 | 2018-11-30 | 武汉钢铁集团鄂城钢铁有限责任公司 | A kind of economical high-ductility 360MPa level structure steel plate and its manufacturing method |
| CN112501504A (en) * | 2020-11-13 | 2021-03-16 | 南京钢铁股份有限公司 | BCA 2-grade container ship crack arrest steel plate and manufacturing method thereof |
| CN114525457A (en) * | 2022-02-27 | 2022-05-24 | 湖南华菱湘潭钢铁有限公司 | Thick-specification low-temperature steel for ship containing liquefied petroleum gas and liquid ammonia and production method thereof |
| CN114752860A (en) * | 2022-04-28 | 2022-07-15 | 湖南华菱湘潭钢铁有限公司 | Production method of E51 thick steel plate with high crack resistance |
| CN114892107A (en) * | 2022-04-28 | 2022-08-12 | 湖南华菱湘潭钢铁有限公司 | Production method of E47 thick steel plate with high crack resistance |
| CN114892083A (en) * | 2022-04-28 | 2022-08-12 | 湖南华菱湘潭钢铁有限公司 | Production method of E40 thick steel plate with high crack resistance |
| CN115747673A (en) * | 2022-12-12 | 2023-03-07 | 湖南华菱湘潭钢铁有限公司 | 420E-grade super-thick steel plate and production method thereof |
| CN115807192A (en) * | 2022-12-12 | 2023-03-17 | 湖南华菱湘潭钢铁有限公司 | Low-carbon 420 MPa-level TMCP structural steel and production method thereof |
| CN115976424A (en) * | 2022-12-14 | 2023-04-18 | 南阳汉冶特钢有限公司 | DH40 crack arrest steel plate for ocean platform and production method thereof |
| CN115976424B (en) * | 2022-12-14 | 2024-03-08 | 南阳汉冶特钢有限公司 | DH40 crack-arrest steel plate for ocean platform and production method thereof |
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Application publication date: 20200616 |